Ferroelectric thin film and method of manufacturing the same

Abstract: This invention includes lead titanate containing La, and at least an element which forms a six-coordinate bond with oxygen atoms and which is selected from the group consisting of Mg and Mn. Accordingly, this invention provides a ferroelectric thin film which is imparted with a high c-axis orientation property while the film is formed. In addition, this thin film does not require a polarization process as with a bulk crystal. The ferroelectric thin film is manufactured by the steps of: positioning a MgO single crystal substrate 9 disposed in advance with a foundation platinum electrode by a sputtering method on the surface of a substrate heater 10, exhausting a chamber 7, heating the substrate by the substrate heater 10, letting in sputtering gases Ar and O₂ through a nozzle 14 into the chamber 7, and maintaining a high degree of vacuum. Then, high frequency electric power is input to a target 1 from a high frequency electric power source 8 to generate plasma, and a film is formed on the substrate 9. In this way, a ferroelectric thin film containing, for example, [(1-x)·Pb 1-y La y Ti 1-y/4 O₃+x·MgO], where x=0.01∼0.10 and y=0.05∼0.25 can be manufactured.

Description: This invention relates to a ferroelectric thin film which is used e.g. for apyroelectric infrared detecting element or a piezoelectric element, and further relates to a method of manufacturing the ferroelectric thin film. A ferroelectric material is characterized by the presence of spontaneous polarization, even when the material is not in an electric field. This phenomenon arises from the presence of permanently-polarized dielectrics forming lines parallel or antiparallel within the material. In addition, the direction of polarization can be reversed by application of an external electric field. By taking advantage of this- property, a ferroelectric material can be applied to various electronic components, such as a pyroelectric infrared detecting element, a piezoelectric element, a light modulator using electro-optical characteristics, or to a non-volatile memory element. A typical example of a well-known ferroelectric material is a perovskite crystal structure oxide, e.g., PbTiO 3 , Pb 1-X La X Ti 1-X/4 O 3 (PLT), PbZr x Ti 1-X O 3 (PZT), and BaTiO 3 . Among these oxides, a PbTiO 3 type ferroelectric material is thought to be a promising pyroelectric material because of its high Curie temperature, large pyroelectric coefficient, preferably small dielectric constant, and small dielectric loss. This material is already put to practical use in the form of an infrared sensor using ceramics. Merits of this pyroelectric infrared sensor are that the operation can take place at room temperature, and the sensor has no wavelength dependency. Besides, the pyroelectric infrared sensor is superior among thermal type infrared sensors with respect to sensitivity and response speed. At present, most ferroelectric materials used for an infrared detecting element or a piezoelectric element are polycrystalline ceramics. Along with the recent tendency of electronic components towards compact size, smaller electronic components compatible with ferroelectric materials are also demanded. Furthermore, since a pyroelectric element is formed thinner, heat capacity decreases and sensitivity increases accordingly. Therefore, due to the need for improved performance of an infrared detecting element, and also because of the development towards smaller and lighter components as mentioned above, the formation of a ferroelectric single crystal thin film which can achieve high sensitivity and high speed response has been drawing attention. For example, a pyroelectric infrared sensor using a PbTiO 3 type thin film of c-axis orientation is reported in J. Appl. Phys., Vol. 61, P. 411 (1987). Also, a ferroelectric thin film is disclosed in JP-A-59-138004 which discloses improved performance index by adding a small amount of La 2 O 3 to PbTiO 3 . Furthermore, as disclosed in JP-A- 59-141427, a small amount of MnO 2 is added to PbTiO 3 for improving figure of merit and dielectric loss of a ferroelectric thin film. In addition, JP-A- 61-88403 discloses a mono phase ferroelectric PbTiO 3 thin film having a high electro-optical effect by selecting a Pb/Ti molar ratio in the PbTiO 3 , and also having pyroelectricity and piezoelectricity. Also, it is disclosed in JP-A- 3-245406 that a small amount of MgO is added to PbTiO 3 for obtaining a ferroelectric thin film having a high direct current resistivity and a high pyroelectric coefficient. In the various conventional techniques mentioned above for forming thin films by using PbTiO 3 type materials, there has been some improvement made regarding pyroelectric characteristics or piezoelectric characteristics as well as with regard to resistivity, withstand voltage, and dielectric loss. However, a thin film which has satisfactory characteristics in all respects has not yet been obtained. It is an object of this invention to solve the above-mentioned conventional problems by providing a ferroelectric thin film which possesses a high c-axis orientation property, and also which does not require a polarization process such as with a bulk crystal. Another object of this invention is to provide a method of manufacturing the ferroelectric thin film. In order to accomplish these and other objects and advantages, the ferroelectric thin film of the first embodiment of this invention comprises a ferroelectric thin film comprising lead titanate containing La, and at least an element which forms a six-coordinate bond with oxygen atoms and which is selected from Mg and Mn. The element Mg is added to form a thin film having a composition of [(1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] (x=0.01∼0.10, y=0.05∼0.25). When Mg and La are added to the composition in an amount less than the above-noted range, the results are poorer. When Mg and La are added to the composition in an amount more than the above-noted range, it tends to have a negative influence on crystal properties and various characteristics such as pyroelectric characteristics. The element Mn is added to form a thin film having a composition of [(1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] (y=0.05∼0.25, z=0.002∼0.05). When Mn and La are added to the composition in an amount less than the above-noted range, the effects are poorer. On the other hand, when Mn and La are added to the composition in an amount more than the above-noted range, it tends to have a negative influence on crystal properties and various characteristics such as pyroelectric characteristics. It is also preferable that the crystal phase of the ferroelectric thin film is a perovskite single phase. As a result, the ferroelectric thin film has an especially high c-axis orientation property and is not conditioned to a polarization process. In addition, it is preferable that the thickness of the ferroelectric thin film is in the range of 100 nm or more and 10 µm or less. When the thickness of the ferroelectric thin film is less than 100 nm, it is generally too thin to establish effective insulation. When the thickness is more than 10 µm, it is less practical since the film formation takes too long. It is preferable that the ferroelectric thin film is a thin film which is not conditioned to a polarization process (as-grown thin film). In a conventional method, it is usually necessary to conduct a polarization process (poling process) with a pyroelectric material under conditions of high temperature and high electric field. However, there is a possibility of the thin film being transformed or decomposed under the conditions of high temperature and high electric field. On the other hand, the thin film of this invention does not require a polarization process, so the thin film can be stably preserved. It is noted that as-grown thin film mentioned above is also called an as-deposited thin film. Furthermore, it is preferable that an orientation rate α of the ferroelectric thin film is 0.85 ≦ α ≦ 1.00 in an X-ray diffraction analysis, provided that the height (intensity) at the (001) peak is I(001), the height (intensity) at the (100) peak is I(100), and α =I(001)/{I(001)+I(100)} . The fact that the orientation rate α is 0.85 ≦ α ≦ 1.00 indicates a high c-axis orientation property of the crystal phase. Conventionally, when a common ceramic lead titanate is used, (101) is the strongest peak, and it can not be oriented to the (001) direction. Furthermore, since the c-axis direction is a polarization axis, the thin film has the property of being oriented to the c-axis. Thus, a polarization process (poling process) after forming the film is no longer necessary. The calculation method of the above-mentioned orientation rate α will be explained in Example 1 which will be described later. Depending on added amounts of La, Mg, and Mn, the orientation rate α varies. It is preferable that Mg is added, where x=0.01∼0.10, and Mn is added, where z=0.002∼0.05. The orientation rate α reaches the highest value by adding Mg, where x=0.02∼0.04, and by adding Mn, where z=0.005∼0.02. On the other hand, the orientation rate α goes down when Mg and Mn are beyond the limits of x=0.01∼0.10 and z=0.002∼0.05. The less La is added, the more the orientation rate α tends to rise. It is also preferable that the ferroelectric thin film is held between two layers of electrode, because this structure is suitable for use as a pyroelectric infrared sensor element. Furthermore, it is preferable that the ferroelectric thin film is used as a pyroelectric material according to claim 7, for a pyroelectric infrared sensor, because this thin film is especially suitable for this particular use. A second embodiment of this invention is a method of manufacturing a ferroelectric thin film according to any one of claims 1-6 comprising lead titanate containing La, and at least an element which forms a six-coordinate bond with oxygen atoms and which is selected from Mg and Mn. The method comprises the steps of: positioning an inorganic single crystal substrate disposed in advance on a foundation platinum electrode by a sputtering method on the surface of a substrate heater, exhausting a chamber, heating the substrate by a substrate heater, letting in sputtering gases into the chamber, maintaining a high degree of vacuum, inputting high frequency electric power to a target or a plurality of different targets from a high frequency electric power source to generate plasma, and forming a film on the substrate. This method can efficiently form the ferroelectric thin film of this invention. It is preferable that the target of the sputtering method is at least one compound having a composition selected from [(1-w)·{(1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO}+w·PbO] and [(1-w)·{(1-x)·(1-y)·PbO+(1-x)y/2·La 2 O 3 +(1-x)(1-y/4)·TiO 2 +x· MgO}+w·PbO] (x=0.01∼0.10, y=0.05∼0.25, w=0.05∼0.40), wherein the number of targets is one or more. This is for the purpose of forming a thin film having the composition of this invention. Furthermore, it is preferable that the target of the sputtering method is at least one compound having a composition selected from [(1-w)·{(1-z)·Pb 1-y La y Ti 1 - y/4 O 3 +Z·MnO 2 }+w·PbO] and [(1-w)·{(1-z)·(1-y)·PbO+(1-z)y/2· La 2 O 3 +(1-z)(1-y/4)·TiO 2 +z·MnO 2 }+w·PbO] (y=0.05∼0.25, z=0.002∼ 0.05, w=0.05∼0.40), and the number of targets is one or more. This is for the purpose of forming a thin film having the composition of this invention. It is also preferable that the target of the sputtering method has a composition at least selected from (A), (B), and (C): (A) a combination of two different targets, wherein at least one target is selected from [(1-w)·Pb 1-y La y Ti 1-y/4 O 3 +w·PbO] and [(1-w)·{(1-y)·PbO+y/2·La 2 O 3 +(1-y/4). TiO 2 }+w·PbO] (y=0.05∼0.25, w=0.05∼0.40), and at least one target is selected from MgO and Mg. (B) a combination of two different targets, wherein at least one target is selected from [(1-w)·{(1-x)· PbTiO 3 +x·MgO}+w·PbO] and [(1-w)·{(1-x)(PbO+TiO 2 )+x·MgO}+w·PbO] (x=0.01∼0.10, w=0.05∼0.40), and one target is La 2 O 3 . (C) a combination of two different targets, wherein at least one target is selected from [(1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] and [(1-x)(1-y)·PbO+(1-x)y/2·La 2 O 3 +(1-x)(1-y/4)·TiO 2 +x·MgO] (x=0.01∼0.10, y=0.05∼0.25), and one target is PbO. In addition, it is preferable that the target of the sputtering method has a composition at least selected from (D), (E), and (F): (D) a combination of two different targets, wherein at least one target is selected from [(1-w)·Pb 1-y La y Ti 1-y/4 O 3 +w·PbO] and [(1-w)·{(1-y)·PbO+y/2·La 2 O 3 +(1-y/4)· TiO 2 }+w·PbO] (y=0.05∼0.25, w=0.05∼0.40), and at least one target is selected from MnO 2 and Mn. (E) a combination of two different targets, wherein at least one target is selected from [(1-w)·{(1-z)· PbTiO 3 +z·MnO 2 }+w·PbO] and [(1-w)·{(1-z)(PbO+TiO 2 )+z·MnO 2 }+w·PbO] (z=0.002∼0.05, w=0.05∼0.40), and one target is La 2 O 3 . (F) a combination of two different targets, wherein at least one target is selected from [(1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] and [(1-z)(1-y)·PbO+(1-z)y/2·La 2 O 3 +(1-z)(1-y/4)·TiO 2 +z·MnO 2 ] (y=0.05∼0.25, z=0.002∼0.05), and one target is PbO. It is preferable that the target of the sputtering method has a composition at least selected from (G), (H), and (I): (G) a combination of three different targets, wherein at least one target is selected from [(1-w)· PbTiO 3 +w·PbO] and [(1-w)·(PbO+TiO 2 )+w·PbO] (w=0.05∼0.40), and one target is La 2 O 3 , and at least one target is selected from MgO and Mg. (H) a combination of three different targets, wherein at least one target is selected from [Pb 1-y La y Ti 1-y/4 O 3 ] and [(1-y)·PbO+y/2·La 2 O 3 +(1-y/4)·TiO 2 ] (y=0.05∼0.25), and one target is PbO, and at least one target is selected from MgO and Mg. (I) a combination of three different targets, wherein at least one target is selected from [(1-x)· PbTiO 3 +x·MgO] and [(1-x)·(PbO+TiO 2 )+x·MgO] (x=0.01∼0.10), and one target is La 2 O 3 , and one target is PbO. Furthermore, it is preferable that the target of the sputtering method has a composition at least selected from (J), (K) , and (L): (J) a combination of three different targets, wherein at least one target is selected from [(1-w)· PbTiO 3 +w·PbO] and [(1-w)·(PbO+TiO 2 )+w·PbO] (w=0.05∼0.40), and one target is La 2 O 3 , and one target is selected from MnO 2 and Mn. (K) a combination of three different targets, wherein at least one target is selected from [Pb 1-y La y Ti 1-y/4 O 3 ] and [(1-y)·PbO+y/2·La 2 O 3 +(1-y/4)·TiO 2 ] (y=0.05∼0.25), and one target is PbO, and one target is selected from MnO 2 and Mn. (L) a combination of three different targets, wherein at least one target is selected from [(1-z)· PbTiO 3 +z·MnO 2 ] and [(1-z)·[(1-z)·(PbO+TiO 2 )+z·MnO 2 ] (z=0.002∼0.05), and one target is La 2 O 3 , and one target is PbO. It is preferable that a plurality of targets used for the sputtering method have four different kinds of combination consisting of (1) one target selected from PbTiO 3 and [PbO+TiO 2 ], (2) one target being La 2 O 3 , (3) one target selected from MgO and Mg, and (4) one target being PbO. This is for the purpose of forming a thin film having the composition of this invention. In addition, it is preferable that a plurality of targets used for the sputtering method have four different types of combinations consisting of (1) one target selected from PbTiO 3 and [PbO+TiO 2 ], and (2) one target being La 2 O 3 , and (3) one target selected from MnO 2 and Mn, and (4) one target being PbO. This is for the purpose of forming a thin film having the composition of this invention. It is also preferable that the target of the sputtering method comprises an oxide formed by press-molding ceramics or powder, or a simple metal plate. These materials are also suitable for the sputtering method. Furthermore, it is preferable that the conditions of the sputtering comprise a temperature of from 550 to 650°C , a pressure of from 0.1 to 2.0 Pa, and an atmosphere gas comprising a mixed gas of argon and oxygen. For example, flow of the mixed gas of argon and oxygen is Ar:O 2 = 9:1 cm 3 /min. A sputtering time depends on thickness of a desired film and on sputtering rate. As an example, it takes 15 hours to form a film having a thickness of 3000 nm with a sputtering rate of 200 nm/h. Accordingly, the ferroelectric thin film described in the above-mentioned invention is formed by using lead titanate containing La, and at least an element which forms a six-coordinate bond with oxygen atoms and which is selected from the group consisting of Mg and Mn. Thus, the thin film is imparted with a high c-axis orientation property while the film is formed. In addition, this thin film does not require a polarization process as with a bulk crystal. Moreover, since the obtained thin film comprises lead titanate containing La and an element which forms a six-coordinate bond with oxygen atoms and which is selected from the group consisting of Mg and Mn, Mg and Mn fill a porous part of the B site which was caused by an additive of La into the A site. As a result, comparing this thin film with a conventional lead titanate thin film, it has excellent electric characteristics as a pyroelectric material, such as dielectric constant ε r, pyroelectric coefficient γ, and dielectric loss tan δ. Moreover, when the thin film was formed in a sputtering method by using a plurality of different targets, the composition can be controlled by controlling the high frequency electric power input to each target. A perovskite crystal structure of PbTiO 3 will be explained by referring to FIG. 5. FIG. 5 is a model view showing an oxygen atom octahedron in the perovskite crystal structure of PbTiO 3 . In FIG. 5, a black ball in the center represents titanium (Ti), white balls with dots represent lead (Pb), and plain white balls represent oxygen (0). The position of titanium (Ti) indicates the B site. Therefore, the B site can be also expressed as the "central position of an oxygen atom octahedron in a perovskite crystal structure". Here, the A site indicates lead (Pb). FIG. 1 is a schematic view showing a manufacturing apparatus of a ferroelectric thin film which is used for embodiments of this invention. FIG. 2 is a schematic view showing a manufacturing apparatus of a ferroelectric thin film which is used for embodiments of this invention. FIG. 3 is a graph showing an x-ray diffraction pattern of a ferroelectric thin film in Example 1 of this invention. FIG. 4 is a schematic cross-sectional view showing a pyroelectric infrared sensor element with use of a ferroelectric thin film in Example 1 of this invention. FIG. 5 is a model view showing an oxygen atom octahedron in a perovskite crystal structure of PbTiO 3 . This invention will be described by referring to the following illustrative examples and attached figures. Example 1 An embodiment will be explained by referring to FIG. 1. In FIG. 1, reference numeral 1 represents a target; 2, a target plate; 3, a magnet; 4, a cover for a brim of target plate 2; 5, a high frequency electrode; 6, an insulator; 7, a vacuum chamber; 8, a high frequency electric power source; 9, a substrate; 10, a substrate heater; 11, a metal mask; 12 and 13, valves; 14, a nozzle for providing sputter gas into vacuum chamber 7; 15, a motor for rotating substrate heater 10; and 32, a bearing with a seal. The method of manufacturing the ferroelectric thin film is as follows. As shown in FIG. 1, the ferroelectric thin film of this invention is manufactured by a high frequency magnetron sputtering method. First, target 1 used for sputtering was manufactured in the following method. PbO, La 2 O 3 , TiO 2 , and MgO in powder form were mixed to attain a target composition comprising {(1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x· MgO} (x=0.01∼0.10, y=0.05∼0.25). Then, the mixed powder was calcined four hours at a temperature of 750°C and smashed. Or, PbO, La 2 O 3 , TiO 2 , and MgO in powder form were mixed to attain {(1-x)(1-Y)·PbO+(1-x)y/2·La 2 O 3 +(1-x)(1-y/4)·TiO 2 +x·MgO} and smashed. To each of these powders, PbO powder with an excess of 5 to 40 mol % was mixed to prevent a Pb deficiency and to attain [(1-w)· {(1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO}+w·PbO] or [(1-w)·{(1-x)·(1-y)· PbO+(1-x)y/2·La 2 O 3 +(1-x)(1-y/4)·TiO 2 +x·MgO}+w·PbO] (x=0.01∼0.10, y=0.05∼0.25, w=0.05∼0.40). After 30 g of each powder was filled in target plate 2, a face pressure of about 250 kgf/cm 2 was provided with a hydraulic press to form target 1. The thin films obtained in these two different manufacturing methods showed equal characteristics. Next, target plate 2 was placed on top of magnet 3, and cover 4 was placed thereon. Here, magnet 3 and high frequency electrode 5 disposed under the magnet are insulated from vacuum chamber 7 by insulator 6. 'Also, high frequency electrode 5 is connected to high frequency electric power source 8. Substrate 9 of the thin film comprised a MgO single crystal substrate (20 mm x 20 mm, thickness 0.5 mm) oriented to (100). On one side of substrate 9, a foundation electrode composed of platinum which had been priority oriented to (100) was formed by a sputtering method with a thickness of 100 nm, and was patterned. After substrate 9 was positioned on substrate heater 10, stainless metal mask 11 of 0.2 mm thick was disposed on the surface of substrate 9. Then, chamber 7 was exhausted, and substrate 9 was heated up to 600°C by substrate heater 10. Substrate heater 10 was rotated by motor 15. After the heating step, valves 12 and 13 were opened to let in sputter gas of Ar and O 2 in a ratio of 9:1 through nozzle 14 into chamber 7 where a degree of vacuum was maintained at 0.5 Pa. Then, when high frequency electric power of 2.1 W/cm 2 (13.56 MHz) was input from high frequency electric power source 8 to generate plasma, a film was formed on substrate 9. In this way, a ferroelectric thin film composed of [(1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] (x=0.01∼0.10, y=0.05∼0.25) was produced. The thin film obtained had a thickness of about 1 µm after five hours of deposition time. On top of this ferroelectric thin film, a Ni-Cr electrode was formed by a DC sputtering method for the purpose of measurement and was patterned. When this thin film was obtained, a solid capacity of each element was measured by an x-ray microanalyzer, and a crystal phase and a c-axis orientation rate α (=I(001)/{I(001)+I(100)}) were measured by an x-ray diffracting method. A graph of an x-ray diffraction is shown in FIG. 3. The measurement was conducted in the range of 20° to 50° . In FIG. 3, A indicates (001) peak of a thin film composed of [0.96(Pb 0.9 La 0.1 Ti 0.975 O 3 ) +0.04 MgO], B indicates (100) peak of the same thin film composed as above, C indicates a peak of a MgO monocrystal substrate, D indicates (002) peak of a thin film composed of [0.96(Pb 0.9 La 0.1 Ti 0.975 O 3 )+0.04 MgO], and E indicates a combined peak of (200) of the same thin film composed as above and Pt of a foundation electrode. Next, calculation method of α a will be explained. Referring to FIG. 3, intensity (height) I(001) of (001) peak shown as A and intensity (height) I(100) of (100) peak shown as B are measured from the chart, and α is calculated according to a calculation formula of α =I(001)/{I(001)+I(100)} . The thin film shown in FIG. 3 had α =0.936. As described above, only (001), (100), and their high-order peaks were confirmed. When α was calculated according to this result, an as-grown thin film was in the range of 0.85 ≦ α ≦ 1.00 and showed a high c-axis orientation property. Furthermore, the solid capacity of MgO was almost equivalent to the amount of MgO in the target composition. Also, the crystal phase comprised a perfect perovskite single phase. Next, pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of the obtained thin film were measured. Tables 1 and 2 show pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of the thin film in each composition. Table 2 also indicates a bulk value of PbTiO 3 . The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-x)· Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] (x=0∼0.10, y=0.05∼0.25) (One kind of target) Composition (1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) X=0 Y=0.05 4.0 × 10 -8 170 0.8 X=0.01 Y=0.05 4.2 × 10 -8 150 0.6 X=0.02 Y=0.05 6.0 × 10 -8 135 0.6 X=0.04 Y=0.05 7.5 × 10 -8 110 0.5 X=0.06 Y=0.05 7.0 × 10 -8 115 0.5 X=0.08 Y=0.05 7.2 × 10 -8 120 0.5 X=0.10 Y=0.05 6.8 × 10 -8 135 0.4 X=0 Y=0.10 5.0 × 10 -8 220 1.0 X=0.01 Y=0.10 5.5 × 10 -8 200 0.8 X=0.02 Y=0.10 7.5 × 10 -8 180 0.6 X=0.04 Y=0.10 9.0 × 10 -8 160 0.6 X=0.06 Y=0.10 9.5 × 10 -8 140 0.5 X=0.08 Y=0.10 9.2 × 10 -8 145 0.5 X=0.10 Y=0.10 9.0 × 10 -8 150 0.6 X=0 Y=0.15 6.5 × 10 -8 310 1.1 X=0.01 Y=0.15 7.8 × 10 -8 300 0.9 X=0.02 Y=0.15 9.8 × 10 -8 270 0.6 X=0.04 Y=0.15 12 × 10 -8 240 0.8 X=0.06 Y=0.15 13 × 10 -8 210 0.7 X=0.08 Y=0.15 12 × 10 -8 195 0.6 X=0.10 Y=0.15 10 × 10 -8 205 0.6 The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-x)· Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] (x=0∼0.10, y=0.05∼0.25) (One kind of target) Composition (1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) X=0 Y=0.20 9.5 × 10 -8 600 1.2 X=0.01 Y=0.20 11 × 10 -8 530 1.0 X=0.02 Y=0.20 14 × 10 -8 455 0.8 X=0.04 Y=0.20 16 × 10 -8 410 0.7 X=0.06 Y=0.20 17 × 10 -8 380 0.8 X=0.08 Y=0.20 18 × 10 -8 355 0.6 X=0.10 Y=0.20 16 × 10 -8 470 0.7 X=0 Y=0.25 6.0 × 10 -8 1500 1.5 X=0.01 Y=0.25 7.0 × 10 -8 1050 1.2 X=0.02 Y=0.25 8.0 × 10 -8 880 1.2 X=0.04 Y=0.25 10 × 10 -8 715 1.0 X=0.06 Y=0.25 12 × 10 -8 620 0.8 X=0.08 Y=0.25 11 × 10 -8 650 0.8 X=0.10 Y=0.25 10 × 10 -8 865 0.8 PbTiO 3 (bulk) 2.0 × 10 -8 190 0.8 As clearly shown in the above-noted Tables 1 and 2, when the added amount y of La was varied from 0.05 to 0.25 and the added amount x of MgO was varied from 0.01 to 0.10, it was confirmed that the sample had a larger γ and smaller ε r and tanδ compared with samples of x=0 and with the bulk value. As described above, it was confirmed that a ferroelectric thin film comprising the composition of this invention is an extremely excellent material which has improved γ and reduced ε r and tan δ, when comparing these values with those of thin films having a composition outside the scope of this invention, and also compared with the bulk value of conventional PbTiO 3 . Next, FIG. 4 shows a ferroelectric thin film of this invention used as a pyroelectric material of a pyroelectric infrared sensor. In FIG. 4, reference numeral 40 represents a pyroelectric infrared sensor element; 41 represents a MgO single crystal substrate of 0.5 mm thick; 42 represents a Pt lower electrode of 100 nm thick; 43 represents a ferroelectric thin film having a thickness of 1µm and composed of [0.96(Pb 0.9 La 0.1 1 Ti 0.975 O 3 )+0.04 MgO]; and 44 represents a Ni-Cr upper electrode of 50 nm thick. According to this structure, the pyroelectric infrared sensor element has a high c-axis orientation property while the film is formed, and it is also unnecessary to conduct a polarization process as with a bulk crystal. Example 2 A method of manufacturing the ferroelectric thin film is as follows. As shown in FIG. 1, the ferroelectric thin film of this invention is manufactured by a high frequency magnetron sputtering method. First, target 1 used for sputtering was manufactured in the following method. PbO, La 2 O 3 , TiO 2 , and MnO 2 in powder form were mixed to attain a target composition comprising {(1-z)·Pb. 1-y La y Ti 1-y/4 O 3 +z· MnO 2 } (y=0.05∼0.25, z=0.002∼0.05). Then, the mixed powder was calcined four hours at a temperature of 750°C and smashed. Or, PbO, La 2 O 3 , TiO 2 , and MnO 2 in powder form were mixed to attain {(1-z)(1-y)·PbO+(1-z)y/2·La 2 O 3 +(1-z)(1-y/4)·TiO 2 +z·MnO 2 } and smashed. To each of these powders, PbO powder with an excess of 5 to 40 mol % was mixed to prevent a Pb deficiency and to attain [(1-w)·{(1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 }+w·PbO] or [(1-w)·{(1-z)· (1-y)·PbO+(1-z)y/2·La 2 O 3 +(1-z)(1-y/4)·TiO 2 +z·MnO 2 }+w·PbO] (y=0.05∼0.25, z=0.002∼0.05, w=0.05∼0.40). After 30 g of each powder was filled in target plate 2, a face pressure of about. 250 kgf/cm 2 was provided with a hydraulic press to form target 1. The thin films obtained in these two different manufacturing methods showed equal characteristics. Next, target plate 2 was placed on top of magnet 3, and cover 4 was placed thereon. Here, magnet 3 and high frequency electrode 5 disposed under the magnet are insulated from vacuum chamber 7 by insulator 6. Also, high frequency electrode 5 is connected to high frequency electric power source 8. Substrate 9 of the thin film comprised a MgO single crystal substrate (20 mm x 20 mm, thickness 0.5 mm) oriented to (100). On one side of substrate 9, a foundation electrode composed of platinum which had been priority oriented to (100) was formed by a sputtering method and was patterned. After substrate 9 was positioned on substrate heater 10, a stainless metal mask 11 (0.2 mm thick) was disposed on the surface of substrate 9. Then, chamber 7 was exhausted, and substrate 9 was heated up to 600°C by substrate heater 10. Substrate heater 10 was rotated by motor 15. After the heating step, valves 12 and 13 were opened to let in sputter gas of Ar and O 2 in a ratio of 9:1 through nozzle 14 into chamber 7 where a degree of vacuum was maintained at 0.5 Pa. Then, when a high frequency electric power of 2.1 W/cm 2 (13.56 MHz) was input from high frequency electric power source 8 to generate plasma, a film was formed on substrate 9. In this way, a ferroelectric thin film composed of [(1-z)·Pb 1-y La y Ti 1y/4 O 3 +z·MnO 2 ] (y=0.05∼0.25, z=0.002∼0.05) was produced. The thin film obtained had a thickness of about 0.95µm after five hours of deposition time. On top of this ferroelectric thin film, a Ni-Cr electrode was formed by a DC sputtering method for the purpose of measurement and was patterned. When this thin film was obtained, the solid capacity of each element was measured by an x-ray microanalyzer, and the crystal phase and the c-axis orientation rate a (=I(001)/{I(001)+I(100)}) were measured by an x-ray diffracting method. As a result, the solid capacity of MnO 2 was almost equivalent to the amount of MnO 2 in the target composition. Furthermore, the crystal phase comprised a perfect perovskite single phase in which only (001), (100), and their high-order peaks were confirmed. Based on this result, when α was calculated, an as-grown thin film was in the range of 0.84 ≦ α ≦ 1.00 and showed a high c-axis orientation property. Next, pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of this thin film were measured. Tables 3 and 4 show pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of the obtained thin film in each composition. Table 4 also indicates the bulk value of PbTiO 3 . The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-z)· Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] (y=0.05∼0.25, z=0∼0.05) (One kind of target) Composition (1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) Y=0.05 z=0 4.0 × 10 -8 175 0.8 Y=0.05 z=0.002 5.2 × 10 -8 130 0.8 Y=0.05 z=0.005 6.8 × 10 -8 120 0.6 Y=0.05 z=0.01 7.3 × 10 -8 115 0.5 Y=0.05 z=0.02 6.9 × 10 -8 125 0.6 Y=0.05 z=0.03 5.7 × 10 -8 140 0.6 Y=0.05 z=0.05 5.2 × 10 -8 155 0.7 Y=0.10 z=0 5.0 × 10 -8 220 1.0 Y=0.10 z=0.002 6.8 × 10 -8 195 0.9 Y=0.10 z=0.005 7.6 × 10 -8 150 0.7 Y=0.10 z=0.01 9.2 × 10 -8 140 0.6 Y=0.10 z=0.02 8.9 × 10 -8 155 0.6 Y=0.10 z=0.03 8.1 × 10 -8 170 0.6 Y=0.10 z=0.05 7.2 × 10 -8 190 0.8 Y=0.15 z=0 6.7 × 10 -8 305 1.2 Y=0.15 z=0.002 8.6 × 10 -8 280 1.0 Y=0.15 z=0.005 10 × 10 -8 240 0.8 Y=0.15 z=0.01 12 × 10 -8 200 0.6 Y=0.15 z=0.02 11 × 10 -8 225 0.6 Y=0.15 z=0.03 9.5 × 10 -8 250 0.7 Y=0.15 z=0.05 8.3 × 10 -8 275 0.9 The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-z)· Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] (y=0.05∼0.25, z=0∼0.05) (One kind of target) Composition (1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) Y=0.20 z=0 9.6 × 10 -8 610 1.3 Y=0.20 z=0.002 12 × 10 -8 455 1.1 Y=0.20 z=0.005 15 × 10 -8 375 1.0 Y=0.20 z=0 01 17 × 10 -8 345 0.8 Y=0.20 z=0.02 15 × 10 -8 380 0.7 Y=0.20 z=0.03 13 × 10 -8 435 0.8 Y=0.20 z=0.05 12 × 10 -8 470 1.0 Y=0.25 z=0 5.9 × 10 -8 1450 1.6 Y=0.25 z=0.002 7.2 × 10 -8 1050 1.3 Y=0.25 z=0.005 9.5 × 10 -8 870 1.0 Y=0.25 z=0.01 12 × 10 -8 620 0.8 Y=0.25 z=0.02 10 × 10 -8 755 0.9 Y=0.25 z=0.03 9.2 × 10 -8 890 1.1 Y=0.25 z=0.05 8.0 × 10 -8 945 1.2 PbTiO 3 (bulk) 2.0 × 10 -8 190 0.8 As clearly shown in the above-noted Tables 3 and 4, when the added amount y of La was varied from 0.05 to 0.25 and the added amount z of MnO 2 was varied from 0.002 to 0.05, it was confirmed that the sample had a larger γ and smaller εr and tanδ compared with samples of z=0 and with the bulk value. As described above, a thin film comprising the composition of this invention is a remarkably extremely excellent material which has improved γ and reduced εr and tanδ, when comparing these values with those of thin films having a composition outside the scope of this invention, and also compared with the bulk value of conventional PbTiO 3 . Example 3 In FIG. 2, reference numerals 16, 17, 18, and 19 represent targets; 20, 21, 22, and 23, high frequency electric power sources; 24, a vacuum chamber; 25, a substrate; 26, a substrate heater; 27, a metal mask; 28 and 29, valves; 30, a nozzle for providing sputter gas into vacuum chamber 24; and 31, a motor for rotating substrate heater 26. In this figure, elements in the vicinity of the target, such as cover, electrode, insulator, and magnet described in FIG. 1 are omitted. A method of manufacturing the ferroelectric thin film is as follows. As shown in FIG. 2, the ferroelectric thin film of this invention was manufactured by a polyphyletic high frequency magnetron sputtering method having four targets. These four targets form a concentric circle and are equidistant from the substrate disposed in the center of the heater. As for targets used for sputtering, two different kinds of target were used; that-is, target 16, (Pb, La)TiO 3 powder, and target 17, MgO ceramics. Among them, target 16 of (Pb, La)TiO 3 powder was formed by the following method. PbO, La 2 O 3 , and TiO 2 , in powder form were mixed to attain a target composition comprising Pb 1-y La y Ti 1-y/4 O 3 (y=0.05∼0.25). Then, the mixed powder was calcined four hours at a temperature of 750°C and smashed. Or, PbO, La 2 O 3 , and TiO 2 in powder form were mixed to attain [(1-y)·PbO+(1-z)y/2·La 2 O 3 +(1-y/4)·TiO 2 ] and smashed. To each of these powders, PbO powder with an excess of 5 to 40 mol % was mixed respectively to prevent Pb from lacking and to attain [(1-w)·Pb 1-y La y Ti 1-y/4 O 3 +w·PbO] or [(1-w)·{(1-y)· Pbo+y/2·La 2 O 3 +(1-y/4)·TiO 2 }+w·PbO] (y=0.05∼0.25, w=0.05∼0.40). After 30 g of each powder was filled in a target plate, a face pressure of about 250 kgf/cm 2 was provided with a hydraulic press to form target 16. The thin films obtained at target 16 by means of these two different manufacturing methods showed equal characteristics. Target 16 and ceramic target 17 composed of MgO ceramics were positioned in chamber 24. In addition, targets 16 and 17 are respectively connected to high frequency electric power sources 20 and 21. Substrate 25 comprised a MgO single crystal substrate (20 mm x 20 mm, thickness 0.5 mm) oriented to (100). On one side of substrate 25, a foundation electrode composed of platinum which had been priority oriented to (100) was formed by a sputtering method and was patterned. After substrate 25 was positioned on substrate heater 26, stainless metal mask 27 of 0.2 mm thick was disposed on the surface of substrate 25. Then, chamber 24 was exhausted, and substrate 25 was heated up to 600°C by substrate heater 26. After the heating step, substrate heater 26 was rotated by motor 31, and valves 28 and 29 were opened to let in sputtering gases Ar and O 2 in a ratio of 9:1 through nozzle 30 into chamber 24 where the degree of vacuum was maintained at 0.5 Pa. Then, high frequency electric power was input from high frequency electric power sources 20 and 21 into targets 16 and 17 to generate plasma, and a film was formed on substrate 25. As for this high frequency electric power input, high frequency electric power source 20 of target 16 was fixed at 2.1 W/cm 2 (13.56 MHz), and high frequency electric power source 21 of target 17 was varied optionally from 0 to 1.2 W/cm 2 (13.56 MHz). By doing so, the added amount of MgO was controlled. In this way, a ferroelectric thin film composed of [(1-x)·Pb 1 - y La y Ti 1-y/4 O 3 +xMgO] (x=0.01∼0.10, y=0.05∼0.25) was produced. The thin film obtained had a thickness of about 1.2µm after five hours of deposition time. On top of this ferroelectric thin film, a Ni-Cr electrode was formed as an upper electrode by a DC sputtering method for the purpose of measurement and was patterned. When this thin film was obtained, the solid capacity of each element was measured by an x-ray microanalyzer, and the crystal phase and c-axis orientation rate α (=I(001)/{I(001)+I (100)}) were measured by an x-ray diffracting method. As a result, the crystal phase comprised a perfect perovskite single phase in which only (001), (100), and their high-order peaks were confirmed. Based on this result, when α was calculated, an as-grown thin film was in the range of 0.84 ≦ α ≦ 1.00 and showed a high c-axis orientation property. Next, pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of the obtained thin film were measured between the foundation electrode and the upper electrode. Tables 5 and 6 show pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of the thin film in each composition. Table 6 also indicates the bulk value of PbTiO 3 . The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-x)· Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] (x=0∼0.10, y=0.05∼0.25) (Two kinds of target) Composition (1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) X=0 Y=0.05 3.9 × 10 -8 175 0.9 X=0.01 Y=0.05 4.5 × 10 -8 150 0.7 X=0.02 Y=0.05 5.8 × 10 -8 140 0.6 X=0.04 Y=0.05 7.4 × 10 -8 115 0.5 X=0.06 Y=0.05 7.5 × 10 -8 115 0.4 X=0.08 Y=0.05 7.2 × 10 -8 125 0.4 X=0.10 Y=0.05 6.5 × 10 -8 140 0.5 x=0 Y=0.10 5.1 × 10 -8 230 1.1 X=0.01 Y=0.10 5.8 × 10 -8 205 0.8 X=0.02 Y=0.10 7.3 × 10 -8 175 0.7 X=0.04 Y=0.10 8.8 × 10 -8 155 0.6 X=0.06 Y=0.10 9.2 × 10 -8 140 0.6 X=0.08 Y=0.10 9.0 × 10 -8 145 0.5 X=0.10 Y=0.10 8.8 × 10 -8 155 0.6 X=0 Y=0.15 6.3 × 10 -8 320 1.2 X=0.01 Y=0.15 7.7 × 10 -8 305 0.9 X=0.02 Y=0.15 9.5 × 10 -8 280 0.8 X=0.04 Y=0.15 11 × 10 -8 245 0.7 X=0.06 Y=0.15 12 × 10 -8 215 0.6 X=0.08 Y=0.15 10 × 10 -8 190 0.6 X=0.10 Y=0.15 9.5 × 10 -8 210 0.7 The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-x)· Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] (x=0∼0.10, y=0.05∼0.25) (Two kinds of target) Composition (1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) X=0 Y=0.20 9.2 × 10 -8 595 1.5 X=0.01 Y=0.20 10 × 10 -8 535 1.0 X=0.04 Y=0.20 15 × 10 -8 410 0.8 X=0.06 Y=0.20 17 × 10 -8 375 0.7 X=0.08 Y=0.20 17 × 10 -8 360 0.6 X=0.10 Y=0.20 15 × 10 -8 450 0.7 X=0 Y=0.25 5.9 × 10 -8 1420 1.6 X=0.01 Y=0.25 7.2 × 10 -8 1010 1.3 X=0.02 Y=0.25 8.5 × 10 -8 850 1.2 X=0.04 Y=0.25 9.8 × 10 -8 715 1.0 X=0.06 Y=0.25 11 × 10 -8 620 0.8 X=0.08 Y=0.25 10 × 10 -8 660 0.7 X=0.10 Y=0.25 9.2 × 10 -8 880 0.8 PbTiO 3 (bulk) 2.0 × 10 -8 190 0.8 As clearly shown in the above-noted Tables 5 and 6, when the added amount y of La was varied from 0.05 to 0.25 and the added amount x of MgO was varied from 0.01 to 0.10, it was confirmed that the sample had a larger γ and smaller εr and tanδ compared with samples of x=0 and with the bulk value. As described above, a ferroelectric thin film comprising the composition of this invention is an extremely excellent material which has improved γ and reduced εr and tanδ, when comparing these values -with those of thin films having a composition outside the scope of this invention, and also compared with the bulk value of conventional PbTiO 3 . In this embodiment, the target used for sputtering was a MgO ceramic target. However, it was confirmed that the same results could be attained by using a metal Mg as target and by letting in sputtering gases Ar and O 2 in a ratio of 9:3 into the chamber. Furthermore, although the targets used for sputtering in this embodiment comprised two different kinds, namely, [(1-w)· Pb 1-y La y Ti 1-y/4 O 3 +w·PbO] or [(1-w)·{(1-y)·PbO+y/2·La 2 O 3 +(1-y/4)· TiO 2 }+w·PbO] (y=0.05∼0.25, w=0.05∼0.40) and a MgO target, it was also confirmed that the same results could be attained by combining two different kinds of targets consisting of [(1-w)·{(1-x)·PbTiO 3 +x·MgO}+w·PbO] or [(1-w)·{(1-x)(PbO+TiO 2 )+x·MgO}+w·PbO] (x=0.01∼0.10, w=0.05∼0.40) and a La 2 O 3 target, or by combining two different kinds of targets consisting of [(1-x)·Pb 1-y La y Ti 1 - y/4 O 3 +x·MgO] or [(1-x)(1-y)·PbO+(1-x)y/2·La 2 O 3 +(1-x)(1-y/4)· TiO 2 +x·HgO] (x=0.01∼0.10, y=0.05∼0.25) and a PbO target. Example 4 A method of manufacturing the ferroelectric thin film is as follows. As shown in FIG. 2, the ferroelectric thin film of this invention was manufactured by a polyphyletic high frequency magnetron sputtering method having four targets. These four targets formed a concentric circle and are equidistant from the substrate disposed in the center of the heater. As for targets used for sputtering, two different kinds of target were used; that is, target 16, (Pb, La)TiO 3 powder, and target 17, MnO 2 ceramics, Among them, target 16 of (Pb, La)TiO 3 powder was formed in the following method. PbO, La 2 O 3 , and TiO 2 , in powder form were mixed to attain a target composition comprising Pb 1-y La y Ti 1-y/4 O 3 (y=0.05∼0.25). Then, the mixed powder was calcined four hours at a temperature of 750°C and smashed. Or, PbO, La 2 O 3 , and TiO 2 in powder form were mixed to attain [(1-y)·PbO+(1-z)y/2·La 2 O 3 +(1-y/4)·TiO 2 ] and smashed. To each of these powders, PbO powder with an excess of 5 to 40 mol % was mixed respectively to prevent a Pb deficiency and to attain [(1-w)·Pb 1-y La y Ti 1-y/4 O 3 +w·PbO] or [(1-w)·{(1-y)· PbO+y/2·La 2 O 3 +(1-y/4)·TiO 2 }+w·PbO] (y=0.05∼0.25, w=0.05∼0.40). After 30 g of this powder was filled in a target plate, a face pressure of about 250 kgf/cm 2 was provided with a hydraulic press to form target 16. The thin films obtained at target 16 by means of these two different manufacturing methods showed equal characteristics. Target 16 and target 17 composed of MnO 2 ceramics were positioned in chamber 24. Besides, targets 16 and 17 are respectively connected to high frequency electric power sources 20 and 21. Substrate 25 comprised a MgO single crystal substrate (20 mm x 20 mm, thickness 0.5 mm) oriented to (100). On one side of substrate 25, a foundation electrode composed of platinum which had been priority oriented to (100) was formed by sputtering and was patterned. After substrate 25 was positioned on substrate heater 26, stainless metal mask 27 of 0.2 mm thick was disposed on the surface of substrate 25. Then, chamber 24 was exhausted, and substrate 25 was heated up to 600°C by substrate heater 26. After the heating step, substrate heater 26 was rotated by motor 31, and valves 28 and 29 were opened to let in sputtering gases Ar and O 2 in a ratio of 9:1 through nozzle 30 into chamber 24 where the degree of vacuum was maintained at 0.5 Pa. Then, high frequency electric power was input from high frequency electric power sources 20 and 21 into targets 16 and 17 to generate plasma, and a film was formed on substrate 25. As for this high frequency electric power input, high frequency electric power source 20 of target 16 was fixed at 2.1 W/cm 2 (13.56 MHz), and high frequency electric power source 21 of target 17 was varied optionally from 0 to 0.7 W/cm 2 (13.56 MHz). By doing so, an additive amount of MnO 2 was controlled. In this way, a ferroelectric thin film composed of [(1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z· MnO 2 ] (y=0.05∼0.25, z=0.002∼0.05) was produced. The thin film obtained had a thickness of about 1.15µm after five hours of deposition time. On top of this ferroelectric thin film, a Ni-Cr electrode was formed as an upper electrode by a DC sputtering method for the purpose of measurement and was patterned. When this thin film was obtained, the solid capacity of each element was measured by an x-ray microanalyzer, and the crystal phase and c-axis orientation rate α (=I(001)/{(I(001)+I(100)}) were measured by an x-ray diffracting method. As a result, the crystal phase comprised a perfect perovskite single phase in which only (001), (100), and their high-order peaks were confirmed. Based on this result, when α was calculated, an as-grown thin film was in the range of 0.85 ≦ α ≦ 1.00 and showed a high c-axis orientation property. Next, pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of the obtained thin film were measured between the foundation electrode and the upper electrode. Tables 7 and 8 show pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tanδ of the thin film in each composition. Table 8 also indicates the bulk value of PbTiO 3 . The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-z)· Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] (y=0.05∼0.25, z=0∼0.05) (Two kinds of target) Composition (1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) Y=0.05 z=0 4.2 × 10 -8 180 0.8 Y=0.05 z=0.002 5.5 × 10 -8 140 0.7 Y=0.05 z=0.005 6.8 × 10 -8 125 0.7 Y=0.05 z=0.01 7.5 × 10 -8 110 0.6 Y=0.05 z=0.02 7.0 × 10 -8 130 0.6 y=0.05 z=0.03 5.6 × 10 -8 145 0.7 Y=0.05 z=0.05 5.2 × 10 -8 160 0.8 Y=0.10 z=0 5.3 × 10 -8 230 1.1 Y=0.10 z=0.002 7.0 × 10 -8 200 0.9 Y=0.10 z=0.005 7.7 × 10 -8 155 0.8 Y=0.10 z=0.01 9.1 × 10 -8 135 0.6 Y=0.10 z=0.02 8.5 × 10 -8 160 0.7 Y=0.10 z=0.03 7.9 × 10 -8 175 0.7 Y=0.10 z=0.05 6.8 × 10 -8 190 0.8 Y=0.15 z=0 6.8 × 10 -8 310 1.2 Y=0.15 z=0.002 8.9 × 10 -8 290 0.9 Y=0.15 z=0.005 10 × 10 -8 250 0.8 Y=0.15 z=0.01 12 × 10 -8 215 0.7 Y=0.15 z=0.02 11 × 10 -8 230 0.6 Y=0.15 z=0.03 9.6 × 10 -8 355 0.8 Y=0.15 z=0.05 8.6 × 10 -8 290 0.9 The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-z)· Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] (y=0.05∼0.25, z=0∼0.05) (Two kinds of target) Composition (1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) Y=0.20 z=0 9.4 × 10 -8 630 1.2 Y=0.20 z=0.002 11 × 10 -8 480 1.0 Y=0.20 z=0.005 14 × 10 -8 395 0.9 Y=0.20 z=0.01 17 × 10 -8 355 0.8 Y=0.20 z=0.02 14 × 10 -8 390 0.7 Y=0.20 z=0.03 12 × 10 -8 450 0.9 Y=0.20 z=0.05 10 × 10 -8 480 1.0 Y=0.25 z=0 6.0 × 10 -8 1500 1.5 Y=0.25 z=0.002 7.2 × 10 -8 1180 1.2 Y=0.25 z=0.005 9.4 × 10 -8 920 1.0 Y=0.25 z=0.01 11 × 10 -8 650 0.9 Y=0.25 z=0.02 11 × 10 -8 765 0.8 Y=0.25 z=0.03 9.7 × 10 -8 905 1.0 Y=0.25 z=0.05 8.5 × 10 -8 970 1.1 PbTiO 3 (bulk) 2.0 × 10 -8 190 0.8 As clearly shown in the above-noted Tables 7 and 8, when the added amount y of La was varied from 0.05 to 0.25 and the added amount z of MnO 2 was varied from 0.002 to 0.05, it was confirmed that the sample had a larger γ and smaller εr and tanδ compared with samples of z=0 and with the bulk value. As described above, a ferroelectric thin film comprising the composition of this invention is a remarkably excellent material which has improved γ and reduced εr and tanδ, when comparing these values with those of thin films having a composition outside the scope of this invention, and also compared with the bulk value of conventional PbTiO 3 . In this embodiment, the target used for sputtering was a MnO 2 ceramic target. However, it was confirmed that the same results could be attained by using a metal Mn as target and by letting in sputtering gases Ar and O 2 in a ratio of 9:3 into the chamber. Furthermore, although the targets used for sputtering in this embodiment comprised two different kinds, namely, [(1-w)· Pb 1-y La y Ti 1-y/4 O 3 +w·PbO] or [(1-w)·{(1-y)·PbO+y/2·La 2 O 3 +(1-y/4)· TiO 2 }+w·PbO] (y=0.05∼0.25, w=0.05∼0.40) and a MnO 2 target, it was also confirmed that the same results could be attained by combining two different kinds of targets consisting of [(1-w)·{(1-z)·PbTiO 3 +z·MnO 2 }+w·PbO] or [(1-w)·{1-z)(PbO+TiO 2 )+z·MnO 2 }+w· PbO] (z=0.002∼0.05, w=0.05∼0.40) and a La 2 O 3 target, or by combining two different kinds of targets consisting of [(1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] or [(1-z)(1-y)·PbO+(1-z)y/2·La 2 O 3 +(1-z)(1-y/4)·TiO 2 + z·MnO 2 ] (y=0.05∼0.25, z=0.002∼0.05) and a PbO target. Example 5 As in Example 3, the ferroelectric thin film of this invention was manufactured by a polyphyletic high frequency magnetron sputtering method. As for targets used for sputtering, three different kinds of target were used; that is, target 16, [PbTiO 3 +PbO] powder, target 17, La 2 O 3 ceramics, and target 18, MgO ceramics. Among them, target 16 of (PbTiO 3 +PbO) powder is composed of [(1-w)·PbTiO 3 +w·PbO]or [(1-w)·(PbO+TiO 2 )+w·PbO] (w=0.05∼0.40). Target 16 was formed with the same method as in Examples 1 to 4. These three kinds of target 16, 17, and 18 were positioned in chamber 24, and a thin film was formed in the same manner as in Examples 1 to 4 on the surface of MgO single crystal substrate 25 comprising patterned platinum. As for the high frequency electric power input to each target, target 16 of pressed [PbTiO 3 +PbO] powder was fixed at 2.1 W/cm 2 (13.56 MHz), and target 17 of La 2 O 3 ceramics was varied optionally from 0 to 0.7 W/cm 2 (13.56 MHz), and target 18 of MgO ceramics was varied optionally from 0 W to 1.2 W/cm 2 (13.56 MHz). By doing so, the added amount of La 2 O 3 and of MgO was controlled. In this way, a ferroelectric thin film composed of [(1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x· MgO] (x=0.01∼0.10, y=0.05∼0.25) was produced. The thin film obtained had a thickness of about 1.3µm after five hours of deposition time. On top of this ferroelectric thin film, a Ni-Cr electrode was formed as an upper electrode by a DC sputtering method for the purpose of measurement and was patterned. When this thin film was obtained, the solid capacity of each element was measured by an x-ray microanalyzer, and the crystal phase and c-axis orientation rate α (=I(001)/{I(001)+I(100)}) were measured by an x-ray diffracting method. As a result, the crystal phase comprised a perfect perovskite single phase in which only (001), (100), and their high-order peaks were confirmed. Based on this result, when α was calculated, the as-grown thin film was in the range of 0.85 ≦ α ≦ 1.00 and showed a high c-axis orientation property. Next, pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of this thin film were measured between the foundation electrode and the upper electrode. Tables 9 and 10 show pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of the thin film in each composition. Table 10 also indicates the bulk value of PbTiO 3 . The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-x)· Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] (x=0∼0.10, y=0.05∼0.25) (Three kinds of target) Composition (1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) X=0 Y=0.05 3.5 × 10 -8 165 1.0 X=0.01 Y=0.05 4.0 × 10 -8 155 0.8 X=0.02 Y=0.05 5.5 × 10 -8 135 0.8 X=0.04 Y=0.05 6.8 × 10 -8 120 0.7 X=0.06 Y=0.05 7.2 × 10 -8 110 0.6 X=0.08 Y=0.05 6.8 × 10 -8 120 0.5 X=0.10 Y=0.05 6.1 × 10 -8 140 0.6 X=0 Y=0.10 5.1 × 10 -8 220 1.2 X=0.01 Y=0.10 5.8 × 10 -8 205 1.0 X=0.02 Y=0.10 6.9 × 10 -8 185 0.9 X=0.04 Y=0.10 8.2 × 10 -8 155 0.7 X=0.06 Y=0.10 8.8 × 10 -8 140 0.6 X=0.08 Y=0.10 9.0 × 10 -8 150 0.6 X=0.10 Y=0.10 8.8 × 10 -8 155 0.7 X=0 Y=0.15 6.3 × 10 -8 315 1.3 X=0.01 Y=0.15 7.2 × 10 -8 295 1.1 X=0.02 Y=0.15 9.2 × 10 -8 270 0.9 X=0.04 Y=0.15 9.8 × 10 -8 235 0.8 X=0.06 Y=0.15 11 × 10 -8 200 0.7 X=0.08 Y=0.15 9.8 × 10 -8 195 0.8 X=0.10 Y=0.15 9.1 × 10 -8 210 0.9 The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-x)· Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] (x=0∼0.10, y=0.05∼0.25) (Three kinds of target) Composition (1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) X=0 Y=0.20 9.4 × 10 -8 590 1.5 X=0.01 Y=0.20 10 × 10 -8 525 1.3 X=0.02 Y=0.20 11 × 10 -8 455 1.2 X=0.04 Y=0.20 13 × 10 -8 400 0.9 X=0.06 Y=0.20 14 × 10 -8 370 0.8 X=0.08 Y=0.20 15 × 10 -8 360 0.8 X=0.10 Y=0.20 13 × 10 -8 470 1.0 X=0 Y=0.25 5.5 × 10 -8 1520 1.8 X=0.01 Y=0.25 6.3 × 10 -8 1070 1.5 X=0.02 Y=0.25 7.5 × 10 -8 850 1.3 X=0.04 Y=0.25 8.6 × 10 -8 710 1.2 X=0.06 Y=0.25 9.5 × 10 -8 605 1.0 X=0.08 Y=0.25 9.1 × 10 -8 635 1.1 X=0.10 Y=0.25 8.8 × 10 -8 815 1.2 PbTiO 3 (bulk) 2.0 × 10 -8 190 0.8 As clearly shown in the above-noted Tables 9 and 10, when the added amount y of La was varied from 0.05 to 0.25 and the added amount x of MgO was varied from 0.01 to 0.10, it was confirmed that the sample had a larger γ and smaller εr and tanδ compared with samples of x=0 and with the bulk value. As described above, a ferroelectric thin film comprising the composition of this invention is an extremely excellent material which has improved γ and reduced εr and tanδ, when comparing these values with those of thin films having a composition outside the scope of this invention and with the bulk value of conventional PbTiO 3 . In this embodiment, the target used for sputtering was a MgO ceramic target. However, it was confirmed that the same results could be attained by using a metal Mg as target and by letting in sputtering gases Ar and O 2 in a ratio of 9:3 into the chamber. Furthermore, although the targets used for sputtering comprised three different kinds, namely, [(1-w)·PbTiO 3 +w·PbO] or [(1-w)·(PbO+TiO 2 )+w·PbO] (w=0.05∼0.40), a La 2 O 3 target, and a MgO target, it was also confirmed that the same results could be attained by combining three different kinds of target consisting of [Pb 1-y La y Ti 1-y/4 O 3 ] or [(1-y)·PbO+y/2·La 2 O 3 +(1-y/4)·TiO 2 ] (y=0.05∼0.25), a PbO target, and a MgO target or a Mg target, or by combining three different kinds of target consisting of [(1-x)· PbTiO 3 +x·MgO] or [(1-x)·(PbO+TiO 2 )+x·MgO] (x=0.01∼0.10), a La 2 O 3 target, and a PbO target. Example 6 As in Example 4, the ferroelectric thin film of this invention was manufactured by a polyphyletic high frequency magnetron sputtering method. As for targets used for sputtering, three different kinds of target were used; that is, target 16, [PbTiO 3 +PbO] powder, target 17, a La 2 O 3 ceramic, and target 18, a MnO 2 ceramic. Among them, target 16 of powder (PbTiO 3 +PbO) is composed of [(1-w)·PbTiO 3 +w·PbO] or [(1-w)·(PbO+TiO 2 )+w·PbO] (w=0.05∼0.40). Target 16 was formed with the same method as in Examples 1 to 4. These three kinds of targets 16, 17, and 18 were positioned in chamber 24, and a thin film was formed in the same manner as in Examples 1 to 4 on the surface of a MgO single crystal substrate 25 comprising patterned platinum. As for the high frequency electric power input to each target, target 16 of pressed [PbTiO 3 +PbO] powder was fixed at 2.1 W/cm 2 (13.56 MHz), and target 17 of La 2 O 3 ceramics was varied optionally from 0 to 0.7 W/cm 2 (13.56 MHz), and target 18 of MnO 2 ceramics was varied optionally from 0 to 0.7 W/cm 2 (13.56 MHz). By doing so, the X added amount of La 2 O 3 and MnO 2 was controlled. In this way, a ferroelectric thin film composed of [(1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z· MnO 2 ] (y=0.05∼0.25, z=0.02∼0.05) was produced. The thin film obtained had a thickness of about 1.26µm after five hours of deposition time. On top of this ferroelectric thin film, a Ni-Cr electrode was formed as an upper electrode by a DC sputtering method for the purpose of measurement and was patterned. When this thin film was obtained, the solid capacity of each element was measured by an x-ray microanalyzer, and the crystal phase and c-axis orientation rate a (=I(001)/{I(001)+I (100)}) were measured by an x-ray diffracting method. As a result, the crystal phase comprised a perfect perovskite single phase in which only (001), (100), and their high-order peaks were confirmed. Based on this result, when α was calculated, the as-grown thin film was in the range of 0.86 ≦ α ≦ 1.00 and showed a high c-axis orientation property. Next, pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of this thin film were measured between the foundation electrode and the upper electrode. Tables 11 and 12 show pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of the thin film in each composition. Table 12 also indicates a bulk value of PbTiO 3 . The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-z)· Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] (y=0.05∼0.25, z=0∼0.05) (Three kinds of target) Composition (1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) Y=0.05 z=0 4.1 × 10 -8 180 0.9 Y=0.05 z=0.002 5.2 × 10 -8 145 0.8 Y=0.05 z=0.005 6.7 × 10 -8 125 0.6 Y=0.05 z=0.01 7.5 × 10 -8 110 0.5 Y=0.05 z=0.02 6.8 × 10 -8 135 0.5 Y=0.05 z=0.03 5.6 × 10 -8 150 0.6 Y=0.05 z=0.05 5.3 × 10 -8 160 0.7 Y=0.10 z=0 5.2 × 10 -8 230 1.1 Y=0.10 z=0.002 7.0 × 10 -8 200 1.0 Y=0.10 z=0.005 7.7 × 10 -8 165 0.8 Y=0.10 z=0.01 9.5 × 10 -8 145 0.6 Y=0.10 z=0.02 8.8 × 10 -8 160 0.7 Y=0.10 z=0.03 7.9 × 10 -8 180 0.7 Y=0.10 z=0.05 7.0 × 10 -8 195 0.8 Y=0.15 z=0 6.8 × 10 -8 320 1.1 Y=0.15 z=0.002 8.8 × 10 -8 295 0.9 Y=0.15 z=0.005 9.8 × 10 -8 250 0.8 Y=0.15 z=0.01 12 × 10 -8 215 0.7 Y=0.15 z=0.02 11 × 10 -8 220 0.6 Y=0.15 z=0.03 10 × 10 -8 240 0.8 Y=0.15 z=0.05 9.2 × 10 -8 280 0.9 The pyroelectric coefficient γ , dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-z)· Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] (y=0.05∼0.25, z=0∼0.05) (Three kinds of target) Composition (1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) Y=0.20 z=0 9.4 × 10 -8 620 1.2 Y=0.20 z=0.002 11 × 10 -8 460 1.0 Y=0.20 z=0.005 14 × 10 -8 375 0.9 Y=0.20 z=0.01 16 × 10 -8 340 0.7 Y=0.20 z=0.02 14 × 10 -8 395 0.8 Y=0.20 z=0.03 12 × 10 -8 430 0.9 Y=0.20 z=0.5 11 × 10 -8 485 1.1 Y=0.25 z=0 6.2 × 10 -8 1480 1.5 Y=0.25 z=0.002 7.2 × 10 -8 1000 1.4 Y=0.25 z=0.005 10 × 10 -8 910 1.2 Y=0.25 z=0.01 12 × 10 -8 660 0.9 Y=0.25 z=0.02 11 × 10 -8 780 0.9 Y=0.25 z=0.03 10 × 10 -8 865 1.0 Y=0.25 z=0.05 9.1 × 10 -8 950 1.2 PbTiO 3 (bulk) 2.0 × 10 -8 190 0.8 As clearly shown in the above-noted Tables 11 and 12, when the added amount y of La was varied from 0.05 to 0.25 and the added amount z of MnO 2 was varied from 0.002 to 0.05, it was confirmed that the sample had a larger γ and smaller εr and tanδ compared with samples of z=0 and with the bulk value. As described above, a ferroelectric thin film comprising the composition of this invention is a remarkably excellent material which has improved γ and reduced εr and tanδ, when comparing these values with those of thin films having a composition beyond the limits of this invention, and also comparing with the bulk value of conventional PbTiO 3 . In this embodiment, the target used for sputtering was a MnO 2 ceramic target. However, it was confirmed that the same results could be attained by using a metal Mn as a target and by letting in sputtering gases Ar and O 2 in a ratio of 9:3 into the chamber. Furthermore, although the targets used for sputtering comprised three different kinds, namely, a target [(1-w)·PbTiO 3 +w· PbO] or [(1-w)·(PbO+TiO 2 )+w·PbO] (w=0.05∼0.40), a La 2 O 3 target, and a MnO 2 target, it was also confirmed that the same results could be attained by combining three different kinds of target consisting of [Pb 1-y La y Ti 1-y/4 O 3 ] or [(1-y)·PbO+y/2·La 2 O 3 +(1-y/4)· TiO 2 ] (y=0.05∼0.25), a PbO target, and a MnO 2 target or a Mn target, or by combining three different kinds of target consisting of [(1-z)·PbTiO 3 +z·MnO 2 ] or [(1-z)·(PbO+TiO) 2 +z·MnO 2 ] (z=0.002∼0.05), a La 2 O 3 target, and a PbO target. Example 7 As in Example 3, the ferroelectric thin film of this invention was manufactured by a polyphyletic high frequency magnetron sputtering method. As for targets used for sputtering, four different kinds of target were used; that is, target 16, PbTiO 3 powder, target 17, a La 2 O 3 ceramic, target 18, a MgO ceramic, and target 19, a PbO ceramic. Among them, target 16 of PbTiO 3 powder is composed of [PbTiO 3 ] or [PbO+TiO 2 ]. Target 16 was formed with the same method as in Examples 1 to 6. These four kinds of targets 16, 17, 18, and 19 were positioned in chamber 24, and a thin film was formed in the same manner as in Examples 1 to 4 on the surface of a MgO single crystal substrate 25 comprising patterned platinum. As for the high frequency electric power input to each target, target 16 of pressed PbTiO 3 powder was fixed at 2.1 W/cm 2 (13.56 MHz), and target 17 of La 2 O 3 ceramics was varied optionally from 0 to 0.7 W/cm 2 (13.56 MHz),and target 18 of MgO ceramics was varied optionally from 0 to 1.2 W/cm 2 (13.56 MHz), and target 19 of PbO ceramics was varied optionally from 0 to 0.5 W/cm 2 (13.56 MHz). By doing so, the added amount of La 2 O 3 and MgO was controlled, and any lacking PbO was supplemented. In this way, a ferroelectric thin film composed of [(1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x· MgO] (x=0.01∼0.10, y=0.05∼0.25) was produced. The thin film -obtained had a thickness of about 1.4µm after five hours of formation time. On top of this ferroelectric thin film, a Ni-Cr electrode was formed as an upper electrode by a DC sputtering method for the purpose of measurement and was patterned. When this thin film was obtained, the-solid capacity of each element was measured by an x-ray microanalyzer, and the crystal phase and c-axis orientation rate α (=I(001)/{I(001)+I(100)}) were measured by an x-ray diffracting method. As a result, the crystal phase comprised a perfect perovskite single phase in which only (001), (100), and their high-order peaks were confirmed. Based on this, when α was calculated, the as-grown thin film was in the range of 0.83 ≦ α ≦ 1.00 and showed a high c-axis orientation property. Next, pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of this thin film were measured between the foundation electrode and the upper electrode. Tables 13 and 14 show pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of the thin film in each composition. Table 14 also indicates the bulk value of PbTiO 3 . The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-x)· Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] (x=0∼0.10, y=0.05∼0.25) (Four kinds of target) Composition (1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) X=0 Y=0.05 4.1 × 10 -8 170 1.0 X=0.01 Y=0.05 4.6 × 10 -8 140 0.9 X=0.02 Y=0.05 6.0 × 10 -8 130 0.7 X=0.04 Y=0.05 7.3 × 10 -8 115 0.6 X=0.06 Y=0.05 7.8 × 10 -8 110 0.5 X=0.08 Y=0.05 7.2 × 10 -8 120 0.6 X=0.10 Y=0.05 6.9 × 10 -8 135 0.7 X=0 Y=0.10 5.2 × 10 -8 235 1.2 X=0.01 Y=0.10 6.0 × 10 -8 215 1.0 X=0.02 Y=0.10 7.5 × 10 -8 190 0.8 X=0.04 Y=0.10 9.0 × 10 -8 175 0.7 X=0.06 Y=0.10 9.5 × 10 -8 150 0.7 X=0.08 Y=0.10 9.0 × 10 -8 145 0.7 X=0.10 Y=0.10 8.5 × 10 -8 160 0.8 X=0 Y=0.15 6.8 × 10 -8 315 1.3 X=0.01 Y=0.15 7.8 × 10 -8 290 1.1 X=0.02 Y=0.15 8.9 × 10 -8 275 0.9 X=0.04 Y=0.15 9.8 × 10 -8 245 0.8 X=0.06 Y=0.15 10 × 10 -8 220 0.8 X=0.08 Y=0.15 11 × 10 -8 195 0.8 X=0.10 Y=0.15 10 × 10 -8 210 0.9 The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-x)· Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] (x=0∼0.10, y=0.05∼0.25) (Four kinds of target) Composition (1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) X=0 Y=0.20 8.8 × 10 -8 620 1.5 X=0.01 Y=0.20 9.5 × 10 -8 545 1.2 X=0.02 Y=0.20 13 × 10 -8 465 1.0 X=0.04 Y=0.20 16 × 10 -8 405 0.9 X=0.06 Y=0.20 16 × 10 -8 370 0.8 X=0.08 Y=0.20 15 × 10 -8 360 0.7 X=0.10 Y=0.20 13 × 10 -8 450 0.8 X=0 Y=0.25 5.8 × 10 -8 1520 1.8 X=0.01 Y=0.25 7.3 × 10 -8 1100 1.5 X=0.02 Y=0.25 8.7 × 10 -8 915 1.3 X=0.04 Y=0.25 10 × 10 -8 730 1.1 X=0.06 Y=0.25 11 × 10 -8 620 0.9 X=0.08 Y=0.25 10 × 10 -8 670 0.8 X=0.10 Y=0.25 9.5 × 10 -8 850 1.0 PbTiO 3 (bulk) 2.0 × 10 -8 190 0.8 As clearly shown in the above-noted Tables 13 and 14, when the added amount y of La was varied from 0.05 to 0.25 and the added amount x of MgO was varied from 0.01 to 0.10, it was confirmed that the sample had a larger γ and smaller εr and tanδ compared with samples of x=0 and with the bulk value. As described above, a ferroelectric thin film comprising the composition of this invention is an extremely excellent material which has improved γ and reduced ε r and tan δ, when comparing these values with those of thin films having a composition outside the scope of this invention, and comparing with the bulk value of conventional PbTiO 3 . In this embodiment, the target used for sputtering was a MgO ceramic target. However, it was confirmed that the same results could be attained by using a metal Mg as target and by letting in sputtering gases Ar and O 2 in a ratio of 9:3 into the chamber. Example 8 As in Example 4, the ferroelectric thin film of this invention was manufactured by a polyphyletic high frequency magnetron sputtering method. As for targets used for sputtering, four different kinds of target were used; that is, target 16, PbTiO 3 powder, target 17, a La 2 O 3 ceramic, target 18, a MnO 2 ceramic, and target 19, a PbO ceramic. Among them, target 16 of PbTiO 3 powder is composed of [PbTiO 3 ] or [PbO+TiO 2 ]. Target 16 was formed with the same method as in Examples 1 to 6. These four kinds of targets 16, 17, 18, and 19 were positioned in chamber 24, and a thin film was formed in the same manner as in Examples 1 to 4 on the surface of a MgO single crystal substrate 25 comprising patterned platinum. As for the high frequency electric power input to each target, target 16 of pressed PbTiO 3 powder was fixed at 2.1 W/cm 2 (13.56 MHz), and target 17 of La 2 O 3 ceramics was varied optionally from 0 to 0.7 W/cm 2 (13.56 MHz),and target 18 of MnO 2 ceramics was varied optionally from 0 to 0.7 W/cm 2 (13.56 MHz), and target 19 of ) PbO ceramics was varied optionally from 0 to 0.5 W/cm 2 (13.56 MHz). By doing so, the added amount of La 2 O 3 and of MnO 2 was controlled, and any lacking PbO was supplemented. In this way, a ferroelectric thin film composed of [(1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z· MnO 2 ] (y=0.05∼0.25, z=0.002∼0.05) was produced. The thin film obtained had a thickness of about 1.38µm after five hours of deposition time. On top of this ferroelectric thin film, a Ni-Cr electrode was formed as an upper electrode by a DC sputtering method for the purpose of measurement and was patterned. When this thin film was obtained, the solid capacity of each element was measured by an x-ray microanalyzer, and the crystal phase and c-axis orientation rate α (=I(001)/{I(001)+I (100))) were measured by an x-ray diffracting method. As a result, the crystal phase comprised a perfect perovskite single phase in which only (001), (100), and their high-order peaks were confirmed. Based on this result, when α was calculated, an as-grown thin film was in the range of 0.84 ≦ α ≦ 1.00 and showed a high c-axis orientation property. Next, pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tanδ of this thin film were measured between the foundation electrode and the upper electrode. Tables 15 and 16 show pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tanδ of the thin film in each composition. Table 16 also indicates the bulk value of PbTiO 3 . The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-z)· Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] (y=0.05∼0.25, z=0∼0.05) (Four kinds of target) Composition (1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) Y=0.05 z=0 4.1 × 10 -8 180 0.9 Y=0.05 z=0.002 5.0 × 10 -8 125 0.8 Y=0.05 z=0.005 6.5 × 10 -8 120 0.6 Y=0.05 z=0.01 7.2 × 10 -8 110 0.6 Y=0.05 z=0.02 7.0 × 10 -8 130 0.7 Y=0.05 z=0.03 5.9 × 10 -8 145 0.8 Y=0.05 z=0.05 5.2 × 10 -8 160 0.9 Y=0.10 z=0 5.3 × 10 -8 210 1.2 Y=0.10 z=0.002 7.0 × 10 -8 180 1.0 Y=0.10 z=0.005 8.0 × 10 -8 155 0.9 Y=0.10 z=0.01 9.2 × 10 -8 135 0.7 Y=0.10 z=0.02 8.5 × 10 -8 150 0.7 Y=0.10 z=0.03 7.8 × 10 -8 170 0.8 Y=0.10 z=0.05 7.0 × 10 -8 180 1.0 The pyroelectric coefficient γ, dielectric constant ε r, and dielectric loss tan δ of a ferroelectric thin film having a composition of [(1-z)· Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ] (y=0.05∼0.25, z=0∼0.05) (Four kinds of target) Composition (1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 pyroelectric coefficient γ (C/cm 2 K) dielectric constant ε r dielectric loss tan δ (%) Y=0.15 z=0 6.8 × 10 -8 310 1.4 Y=0.15 z=0.002 8.8 × 10 -8 285 1.1 Y=0.15 z=0.005 9.9 × 10 -8 230 0.9 Y=0.15 z=0.01 11 × 10 -8 215 0.7 Y=0.15 z=0.02 10 × 10 -8 230 0.7 Y=0.15 z=0.03 9.1 × 10 -8 255 0.8 Y=0.15 z=0.05 8.5 × 10 -8 290 0.9 Y=0.20 z=0 9.4 × 10 -8 600 1.5 Y=0.20 z=0.002 11 × 10 -8 480 1.3 Y=0.20 z=0.005 14 × 10 -8 390 1.1 Y=0.20 z=0.01 16 × 10 -8 355 0.9 Y=0.20 z=0.02 13 × 10 -8 410 0.7 Y=0.20 z=0.03 11 × 10 -8 450 0.8 Y=0.20 z=0.05 10 × 10 -8 510 0.9 Y=0.25 z=0 6.2 × 10 -8 1550 1.7 Y=0.25 z=0.002 7.5 × 10 -8 1120 1.3 Y=0.25 z=0.005 9.2 × 10 -8 950 1.1 Y=0.25 z=0.01 11 × 10 -8 710 0.9 Y=0.25 z=0.02 10 × 10 -8 735 0.8 Y=0.25 z=0.03 9.6 × 10 -8 910 0.9 Y=0.25 z=0.05 8.6 × 10 -8 985 1.1 PbTiO 3 (bulk) 2.0 × 10 -8 190 0.8 As clearly shown in the above-noted Tables 15 and 16, when the added amount y of La was varied from 0.05 to 0.25 and the added amount z of MnO 2 was varied from 0.002 to 0.05, it was confirmed that the sample had a larger γ and smaller εr and tanδ compared with samples of z=0 and with the bulk value. As described above, a ferroelectric thin film comprising the composition of this invention is a remarkably excellent material which has improved γ and reduced εr and tanδ, when comparing these values with those of thin films comprising a composition outside the scope of this invention, and compared with the bulk value of conventional PbTiO 3 . In this embodiment, the target used for sputtering was a MnO 2 ceramic target. However, it was confirmed that the same results could be attained by using a metal Mn as target and by letting in sputter gas of Ar and O 2 in a ratio of 9:3 into the chamber. Furthermore, targets used in Examples 1 to 8 were formed by press-molding powder. The same results could be attained by using ceramic targets having the same composition. Accordingly, the ferroelectric thin film manufactured in the above-mentioned methods of this invention is imparted with a high c-axis orientation property while the film is formed. In addition, this thin film does not require a polarization process as with a bulk crystal. Moreover, since the obtained thin film comprises lead titanate containing La and an element which forms a six-coordinate bond with oxygen atoms and which is selected from the group consisting of Mg and Mn, Mg and/or Mn fill a porous part of the B site which was caused by an additive of La into the A site. As a result, comparing this thin film with a conventional lead titanate thin film added with La, it has excellent electric characteristics as a pyroelectric material, such as dielectric constant ε r, pyroelectric coefficient γ, and dielectric loss tan δ. Moreover, when the thin film was formed in a sputtering method by using a plurality of different targets, a composition can be controlled by controlling the high frequency electric power input to each target. Thus, the invention provides a pyroelectric sensor material which can attain electronic devices of compact size, high sensitivity, and high speed response. Therefore, the ferroelectric thin film and the method of manufacturing the thin film of this invention have extremely high industrial value.

Claims: A ferroelectric thin film having a composition of [(1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO],where x=0.01∼0.10 and y=0.05-0.25, or a composition of [(1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ],where y=0.05-0.25 and z= 0.002-0.05, wherein at least one element selected from Mg and Mn forms a six-coordinate bond with oxygen atoms. The ferroelectric thin film as in claim 1, wherein said ferroelectric thin film has a crystal phase that is a perovskite single phase. The ferroelectric thin film as in any one of claims 1 to 2, wherein said ferroelectric thin film has a thickness of 100 nm or more and 10µm or less. The ferroelectric thin film as in any one of claims 1 to 3, wherein said ferroelectric thin film is a thin film which does not require a polarization process. The ferroelectric thin film as in any one of claims 1 to 4, wherein said ferroelectric thin film has an orientation rate α of 0.85 ≦ α ≦ 1.00 in an X-ray diffraction analysis, provided that the height at (001) peak is I(001), the height at (100) peak is I(100), and α =I(001)/{I(001)+ I(100)}. The ferroelectric thin film as in any one of claims 1 to 5, wherein said ferroelectric thin film is disposed between two layers of electrode. A pyroelectric material for a pyroelectric infrared sensor comprising a ferroelectric thin film according to any one of claims 1 to 6. A method of manufacturing a ferroelectric thin film according to any one of claims 1 to 6, which comprises the steps of: positioning an inorganic single crystal substrate disposed in advance with a foundation platinum electrode by a sputtering method on the surface of a substrate heater, exhausting a chamber, heating the substrate by a substrate heater, letting in sputtering gases into the chamber, maintaining a high degree of vacuum, inputting high frequency electric power to a target or a plurality of different targets from a high frequency electric power source to generate plasma, and forming a film on the substrate. The method of manufacturing a ferroelectric thin film as in claim 8, wherein one or more targets is used for the sputtering, and at least one of the targets comprises at least one compound selected from [(1-w)·{(1-x)· Pb 1-y La y Ti 1-y/4 O 3 +x·MgO}+w·PbO] and [(1-w)·{(1-x)·(1-y)·PbO+(1-x)y/2·La 2 O 3 +(1-x)(1-y/4)·TiO 2 +x·MgO}+w·PbO], where x=0.01∼0.10, y=0.05∼0.25, w=0.05∼0.40. The method of manufacturing a ferroelectric thin film as in claim 8, wherein at least one of the targets for sputtering comprises at least one compound selected from [(1-w)·{(1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 }+w· PbO] and [(1-w)·{(1-z)·(1-y)·PbO+(1-z)y/2·La 2 O 3 +(1-z)(1-y/4)· TiO 2 +z·MnO 2 }+w·PbO], where y=0.05∼0.25, z=0.002∼0.05, w=0.05∼ 0.40. The method of manufacturing a ferroelectric thin film as in claim 8, wherein at least two targets for sputtering comprise at least one composition selected from (A), (B), and (C): (A) a combination of two different targets, wherein at least one target is selected from [(1-w)·Pb 1-y La y Ti 1-y/4 O 3 +w·PbO] and [(1-w)·{(1-y)·PbO+y/2·La 2 O 3 +(1-y/4)· TiO 2 }+w·PbO], where y=0.05∼0.25, w=0.05∼0.40, and at least one target is selected from MgO and Mg. (B) a combination of two different targets, wherein at least one target is selected from [(1-w)·{(1-x)· PbTiO 3 +x·MgO}+w·PbO] and [(1-w)·{(1-x)(PbO+TiO 2 )+x·MgO}+w·PbO], where x=0.01∼0.10, w=0.05∼0.40, and one target is La 2 O 3 . (C) a combination of two target kinds, wherein at least one target is selected from [(1-x)·Pb 1-y La y Ti 1-y/4 O 3 +x·MgO] and [(1-x)(1-y)·PbO+(1-x)y/2·La 2 O 3 +(1-x)(1-y/4)·TiO 2 +x·MgO] (x=0.01∼0.10, y=0.05∼0.25), and one target is PbO. The method of manufacturing a ferroelectric thin film as in claim 8, wherein at least two targets for the sputtering comprise a composition selected from (D), (E), and (F): (D) a combination of two different targets, wherein at least one target is selected from [(1-w)·Pb 1-y La y Ti 1-y/4 O 3 +w·PbO] and [(1-w)·{(1-y)·PbO+y/2·La 2 O 3 +(1-y/4)· TiO 2 }+w·PbO], where y=0.05∼0.25, w=0.05∼0.40, and at least one target is selected from MnO 2 and Mn. (E) a combination of two different targets, wherein at least one target is selected from [(1-w)·{(1-z)· PbTiO 3 +z·MnO 2 }+w·PbO] and [(1-w)·{(1-z)(PbO+TiO 2 )+z·MnO 2 }+w·PbO], where z=0.002∼0.05, w=0.05∼0.40, and one target is La 2 O 3 . (F) a combination of two different targets, wherein at least one target is selected from [(1-z)·Pb 1-y La y Ti 1-y/4 O 3 +z·MnO 2 ]and [(1-z)(1-y)·PbO+(1-z)y/2·La 2 O 3 +(1-z)(1-y/4)·TiO 2 +z·MnO 2 ], where y=0.05∼0.25, z=0.002∼0.05, and one target is PbO. The method of manufacturing a ferroelectric thin film as in claim 8, wherein at least three targets for the sputtering comprise a composition selected from (G), (H), and (I): (G) a combination of three different targets, wherein at least one target is selected from [(1-w)· PbTiO 3 +w·PbO] and [(1-w)·(PbO+TiO 2 )+w·PbO], where w=0.05∼0.40, and one target is La 2 O 3 , and at least one target is selected from MgO and Mg. (H) a combination of three different targets, wherein at least one target is selected from [Pb 1-y La y Ti 1-y/4 O 3 ] and [(1-y)·PbO+y/2·La 2 O 3 +(1-y/4)·TiO 2 ], where y=0.05∼0.25, and one target is PbO, and at least one target is selected from MgO and Mg. (I) a combination of three different targets, wherein at least one target is selected from [(1-x)· PbTiO 3 +x·MgO] and [(1-x)·(PbO+TiO 2 )+x·MgO], where x=0.01∼0.10, and one target is La 2 O 3 , and one target is PbO. The method of manufacturing a ferroelectric thin film as in claim 8, wherein at least three targets of the sputtering comprise a composition selected from (J), (K), and (L): (J) a combination of three different targets, wherein at least one target is selected from [(1-w)· PbTiO 3 +w·PbO] and [(1-w)·(PbO+TiO 2 )+w·PbO], where w=0.05∼0.40, and one target is La 2 O 3 , and at least one target is selected from MnO 2 and Mn. (K) a combination of three different targets, wherein at least one target is selected from [Pb 1-y La y Ti 1-y/4 O 3 ] and [(1-y)· PbO+y/2·La 2 O 3 +(1-y/4)·TiO 2 ], where y=0.05∼0.25, and one target is PbO, and one target is selected from MnO 2 and Mn. (L) a combination of three different targets, wherein at least one target is selected from [(1-z)· PbTiO 3 +z·MnO 2 ] and [(1-z)·(PbO+TiO 2 )+z·MnO 2 ] where z=0.002∼ 0.05, and one target is La 2 O 3 , and one target is PbO. The method of manufacturing a ferroelectric thin film as in claim 8, wherein a plurality of targets is used for the sputtering and comprise four different targets which are (1) one target selected from PbTiO 3 and [PbO+TiO 2 ], (2) one target being La 2 O 3 , (3) one target selected from MgO and Mg, and (4) one target being PbO. The method of manufacturing a ferroelectric thin film as in claim 8, wherein four different targets are used for the sputtering and comprise (1) one target selected from PbTiO 3 and [PbO+TiO 2 ], (2) one target being La 2 O 3 , (3) one target selected from MnO 2 and Mn, and (4) one target being PbO. The method of manufacturing a ferroelectric thin film as in any one of claims 8 to 16, wherein a target of the sputtering comprises an oxide formed by press-molding ceramics or powder, or a metal plate. The method of manufacturing a ferroelectric thin film as in any one of claims 8 to 17, wherein conditions of the sputtering comprise a temperature of from 550 to 650°C, a pressure of from 0.1 to 2.0 Pa, and an atmosphere gas comprising a mixed gas of argon and oxygen.

Inventors: FUJII EIJI, FUJII SATORU, FUJII SATOSHI, KOBUNE MASAFUMI, TAKAYAMA RYOICHI, TOMOZAWA ATSUSHI, FUJII, EIJI, FUJII, SATORU, FUJII, SATOSHI, KOBUNE, MASAFUMI, TAKAYAMA, RYOICHI, TOMOZAWA, ATSUSHI, FUJII, EIJI, MATSUSHITA ELEC. IND. CO., LTD., FUJII, SATORU, MATSUSHITA ELEC. IND. CO., LTD., FUJII, SATOSHI, HIMEJI INSTITUTE OF TECHNOLOGY, TAKAYAMA, RYOICHI, MATSUSHITA ELEC. IND. CO., LTD., TOMOZAWA, ATSUSHI, MATSUSHITA ELEC. IND. CO., LTD.
Applicants: MATSUSHITA ELECTRIC IND CO LTD, MATSUSHITA ELECTRIC INDUSTRIAL CO., LTD.
Application year: 1994
Main classification: C23C14
IPC codes: C23C14, H01L37, H01L41, C04B35, C30B23